US20100126639A1 - Magnesium-contained high-silicon aluminum alloys structural materials and manufacture method thereof - Google Patents

Magnesium-contained high-silicon aluminum alloys structural materials and manufacture method thereof Download PDF

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Publication number
US20100126639A1
US20100126639A1 US12/451,232 US45123208A US2010126639A1 US 20100126639 A1 US20100126639 A1 US 20100126639A1 US 45123208 A US45123208 A US 45123208A US 2010126639 A1 US2010126639 A1 US 2010126639A1
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thermal
aluminum alloys
casting
ingot
plastic processing
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Liang Zuo
Fuxiao Yu
Gang Zhao
Xiang Zhao
Yongliang Yang
Yan Li
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Assigned to NORTHEASTERN UNIVERSITY reassignment NORTHEASTERN UNIVERSITY ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: LI, YAN, YANG, YONGLIANG, YU, FUXIAO, ZHAO, GANG, ZHAO, XIANG, ZUO, LIANG
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent

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  • the present invention relates to aluminum alloys and their method of preparation, and more particularly to magnesium-contained high-silicon aluminum alloys for use as structural materials, and the manufacture method thereof.
  • Aluminum-silicon alloys (Al—Si alloys), especially those with high silicon content, are widely used in car and aviation industries, due to their low density, high wear resistance, high anti-corrosiveness, and low thermal expansion coefficient. With the common solidification method for preparation of Al—Si alloys, there usually appear large silicon particles and eutectic plates, resulting in a dramatically increased brittleness of the alloys. Thus, it is difficult to improve the solidified microstructure and to obtain various shaped high-performance structural materials through subsequent plastic deformation, which poses a bottleneck for more general applications of these alloys. Traditionally, Al—Si alloys are categorized into the casting aluminum alloy series.
  • the above method can be incorporated with thermoplastic processing and subsequent heat treatment, so as to produce Mg-containing high-silicon aluminum alloys with relatively high plasticity and strength, including profiles, bars, sheets, and forgings, for use as advanced new structural materials.
  • An object of the present invention is to provide high-silicon aluminum alloys (Al—Si alloys) that contain magnesium (Mg) and have good plasticity and high strength for use as structural materials, and the manufacture method thereof. Without adding any modifiers, the Al—Si alloys are manufactured at low cost with the direct chill casting followed by the thermoplastic process and heat treatment.
  • the present invention presents the aluminum alloys containing Mg and high Si, which comprises profiles, bars, sheets, and forgings, wherein the aluminum alloys are made by a process comprising the steps of:
  • the Mg-contained high-silicon aluminum alloys for use as structural materials contain 0.2 ⁇ 2.0 wt % of Mg and 8 ⁇ 18 wt % of Si, wherein they have an evenly refined microstructure: the aluminum matrix is fine equiaxed with an average grain size less than 6 ⁇ m, and the silicon and second phase particles are dispersed with an average size less than 5 ⁇ m.
  • the Mg-contained high-silicon aluminum alloys may contain at least one of Cu, Zn, Ni, Ti, and Fe elements, wherein a total weight percentage of the Cu, Zn, Ni, Ti, and Fe is less than 2 wt %.
  • the step (a) of direct chill casting is subjected to the cast ingot preparation for a given Al—Si alloy, at a relative casting temperature of 150 ⁇ 300° C. above the liquidus line, a casting speed of 100 ⁇ 200 mm/min, and a cooling water flux of 5 ⁇ 15 g/mm ⁇ s on the periphery of the solidified ingot, wherein no modifier is added to the alloy.
  • the step (b) of preheat-treating is subjected to the formation of dispersed eutectic Si phase particles in the ingot, at a heating rate of 10 ⁇ 30° C./min, a heating temperature of 450 ⁇ 520° C., and a holding time of 1 ⁇ 3 hours.
  • the preheat-treated ingot is subjected to a thermal-plastic processing in the step (c), at a hot-deformation temperature of 400 ⁇ 520° C., followed by cooling naturally or forcedly.
  • the hot-deformed product is then heat-treated after the thermal-plastic processing.
  • the heat treatment in the step (c) further comprises a step of solution treatment and a step of artificial aging process.
  • the solution treatment is performed at a heating rate of 10 ⁇ 30° C./min, a solution treatment temperature of 500 ⁇ 540° C., and a solution treatment time of 0.5 ⁇ 3 hours, followed by quenching.
  • the artificial aging process is performed at an aging temperature of 160 ⁇ 200° C., and an aging time of 1-10 hours.
  • the heat treatment in the step (c) further comprises a step of artificial or natural aging treatment, wherein the artificial treatment is performed at an aging temperature of 160 ⁇ 200° C., and an aging time of 1 ⁇ 10 hours.
  • a hot rolling process is adapted in the step of thermal-plastic processing, wherein the ingot is hot deformed at a total rolling reduction of more than 40%.
  • a hot extrusion process is adapted in the step of thermal-plastic processing, wherein the ingot is hot deformed at an extrusion ratio of more than 15.
  • a hot forging process is adapted in the step of thermal-plastic processing, wherein the ingot is hot deformed at a forging ratio of more than 40%.
  • the present invention overcomes the cognition prejudice traditionally imposed on Al—Si alloys. Without adding any modifiers, an unexpected effect has been reached on the magnesium-contained high-silicon aluminum alloys prepared by incorporating conventional direct chill casting method with thermal-plastic process and heat treatment. They are typically of fine-dispersed silicon particles and second phase at equiaxed Al matrix, associated with a relatively high strength and good plasticity for potential use as structural materials
  • FIG. 14 gives a comparison of mechanical properties between the Al—Si extrusion alloys of the present invention and the China National Standard extrusion alloy 6063 at the T5 and T6 states, wherein the alloys of the present invention are Al-8.5Si-1.8Mg-0.27Fe, Al-12.7Si-0.7Mg-1.5Cu-0.3Ni-0.3Ti-0.3Fe, and Al-15.5Si-0.7Mg-0.27Fe, respectively.
  • the yield strength and tensile strength of the Al-8.5Si-1.8Mg-0.27Fe, Al-12.7Si-0.7Mg-1.5Cu-0.3Ni-0.3Ti-0.3Fe, and Al-15.5Si-0.7Mg-0.27Fe extrusion alloys at the T6 state are higher than the China National Standards for the extrusion alloy 6063 at the T6 state.
  • the mechanical properties of these alloys at the extrusion state (T1), especially the elongation rate, are also higher than the China National Standards for the 6063 alloys at the T5 state.
  • the 6063 alloys As the most common aluminum extrusion alloys, the 6063 alloys have been widely used in architectures, vehicles, and decorations etc., which have great need in the existing market. Once the 6063 alloys are partially replaced by the magnesium-contained high-silicon aluminum alloys of the present invention, it will bring great economic benefits. In addition, the use of an increased amount of Si in the alloys can dramatically conserve the aluminum resource.
  • FIG. 1 is a perspective view of a device of direct chill casting according to preferred embodiments of the present invention.
  • FIG. 2 is a microstructure of ingot of Al-12.7Si-0.7Mg-0.3Fe alloy (#3) at cast condition during the direct chill casting process according to a first preferred embodiment of the present invention, wherein a casting temperature is 730° C., a casting rate is 180 mm/min, and a cooling water flow rate is 8 g/mm ⁇ s.
  • FIG. 3 is a high magnification microstructure of ingot of Al-12.7Si-0.7Mg-0.3Fe alloy (#3) at cast condition during the direct chill casting process according to the first preferred embodiment of the present invention, wherein a casting temperature is 730° C., a casting rate is 180 mm/min, and a cooling flow rate of the surrounding water is 8 g/mm ⁇ s.
  • FIG. 4 is a microstructure of Al-12.7Si-0.7Mg-0.3Fe alloy (#3) after pre-heated to 500° C. for 2 hours, heat extruded at 470° C. (having extraction ratio of 15) according to a second preferred embodiment of the present invention.
  • FIG. 5 is a T6 state microstructure of Al-12.7Si-0.7Mg-0.3Fe alloy (#3) after pre-heated to 500° C. for 2 hours, heat extruded at 470° C. (having extraction ratio of 15) according to a third preferred embodiment of the present invention, wherein said T6 state is at a solution temperature 540° C. for one hour, and at an artificial aging temperature 200° C. for 3 hours.
  • FIG. 6 is a microstructure of ingot of Al-15.5Si-0.7Mg-0.27Fe alloy (#5) at cast condition during the direct chill casting process according to the first preferred embodiment of the present invention, wherein a casting temperature is 800° C., a casting rate is 140 mm/min, and a cooling water flow rate is 10 g/mm ⁇ s.
  • FIG. 7 is a high magnification microstructure of ingot of Al-15.5Si-0.7Mg-0.27Fe alloy (#5) at cast condition during the direct chill casting process according to the first preferred embodiment of the present invention, wherein a casting temperature is 800° C., a casting rate is 140 mm/min, and a cooling water flow rate is 10 g/mm ⁇ s.
  • FIG. 8 is a microstructure of Al-15.5Si-0.7Mg-0.27Fe alloy (#5) after pre-heated to 500° C. for 2 hours, heat extruded at 470° C. (having extrusion ratio of 45) according to the second preferred embodiment of the present invention.
  • FIG. 9 is a microstructure of Al-15.5Si-0.7Mg-0.27Fe alloy (#5) after pre-heated to 500° C. for 1 hour, heat rolled at 500° C. (pressing amount of 60%) according to the second preferred embodiment of the present invention.
  • FIG. 10 is a T6 state microstructure of ingot of Al-15.5Si-0.7Mg-0.27Fe alloy (#5) after pre-heated to 500° C. for 2 hours, heat extruded at 470° C. (having extraction ratio of 45) according to the third preferred embodiment of the present invention, wherein said T6 state is at a solution temperature 520° C. for 2 hours, and at an artificial aging temperature 180° C. for 4 hours.
  • FIG. 11 is a T6 state microstructure of rectangular ingot of Al-15.5Si-0.7Mg-0.27Fe alloy (#5) after pre-heated to 500° C. for 1 hour, heat rolling at 500° C. (pressing amount of 60%) according to the third preferred embodiment of the present invention, wherein said T6 state is at a solution temperature 520° C. for 3 hours, and at an artificial aging temperature 200° C. for 4 hours.
  • FIG. 12 is a T6 state of high rate microstructure of Al-15.5Si-0.7Mg-0.27Fe alloy (#5) after pre-heated to 500° C. for 2 hours, heat extruded at 470° C. (having extrusion ratio of 45) according to the third preferred embodiment of the present invention, wherein said T6 state is at a solution temperature 520° C. for 2 hours, and at an artificial aging temperature 180° C. for 4 hours.
  • FIG. 13 is a microstructure of ingot of Al-17.5Si-0.7Mg-1.0Cu-0.27Fe alloy (#7) at cast condition during the direct chill casting process according to the first preferred embodiment of the present invention, wherein a casting temperature is 850° C., a casting rate is 120 mm/min, and a cooling water flow rate is 10 g/mm ⁇ s.
  • FIG. 14 is a table showing the comparisons mechanical properties of extrusion Si Al alloy of the present invention and the China standard extrusion of 6063 alloy.
  • FIG. 15 is a table showing the compositions of an alloy made from the ingot via the casting process.
  • FIG. 16 is a table showing the parameters of different alloys through casting process.
  • FIG. 17 is a table showing the parameters of the pre-heating process and extraction process of each of alloys.
  • FIG. 18 is a table showing the parameters of the pre-heating process and rolling process of each of alloys.
  • FIG. 19 is a table showing the parameters of the pre-heating process and forging process of each of alloys.
  • FIG. 20 is a table showing the parameters of the extrusion process for different alloys.
  • FIG. 21 is a table showing the parameters of the rolling process for different alloys.
  • FIG. 22 is a table showing the parameters of the forging process for different alloys.
  • FIG. 23 is a table showing the mechanical properties under variety of deformation processes and heat treatments situations.
  • FIG. 1 of the drawings a step of casting ingot via the direct chill casting method according to a first preferred embodiment of the present invention is illustrated.
  • FIG. 1 of the drawings A device designed for the direct chill casting process is shown in FIG. 1 of the drawings, wherein the device comprises a cooling water inlet 1 , a crystallizer 2 , a hot top 4 , and a graphite ring 5 , wherein a raw material 3 of the ingot and a liquid metal 6 are separately received within a container of the device.
  • FIG. 15 A plurality of compositions of an alloy made from the ingot via the casting process is shown in FIG. 15 .
  • FIG. 16 A plurality of parameters of the casting process is shown in FIG. 16 .
  • FIGS. 17 , 18 , and 19 a step of preheating, followed by hot extruding, or hot rolling, or hot forging the ingot according to a second preferred embodiment of the present invention is illustrated.
  • the ingot is heated in an oven at a predetermined heating rate. After the predetermined temperature is reached, the ingot is held for a predetermined time. Then, a hot extrusion device, or a hot rolling device, or a hot forging device is used to complete a thermal-plastic processing.
  • a plurality of parameters of the preheating and hot extruding for each of the alloys is shown in FIG. 17 .
  • a plurality of parameters of the preheating and hot rolling for each of the alloys is shown in FIG. 18 .
  • a plurality of parameters of the preheating and hot forging for each of the alloys is shown in FIG. 19 .
  • FIGS. 20 , 21 , 22 , and 23 a step of heat treatment after hot deformation of the alloys, such as hot extrusion, hot rolling, and hot forging, according to a third preferred embodiment of the present invention is illustrated.
  • the heat treatment is applied to the product at a predetermined temperature.
  • a plurality of parameters of the hot extrusion, hot rolling, and hot forging processes are shown in FIGS. 20 , 21 , and 22 respectively.
  • a plurality of mechanical properties of the alloys after the heat treatments is shown in FIG. 23 .
  • the present invention provides the industrial use of the Mg-contained high silicon aluminum alloys (Al—Si alloy), and the manufacture method thereof. Without adding any modifiers, the Al—Si alloys having good plasticity and relatively high strength are manufactured at low cost with the direct chill casting followed by the thermal-plastic process and heat treatment, for use as structural materials.

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US12/451,232 2007-06-29 2008-06-30 Magnesium-contained high-silicon aluminum alloys structural materials and manufacture method thereof Abandoned US20100126639A1 (en)

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CN200710011919.0 2007-06-29
CN200710011919 2007-06-29
PCT/CN2008/001246 WO2009003365A1 (fr) 2007-06-29 2008-06-30 Pièce de matériau de structure en alliage d'al contenant mg et à forte teneur en si et procédé de fabrication de celle-ci

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EP (1) EP2172572B1 (ru)
JP (1) JP2010531388A (ru)
KR (1) KR20100018048A (ru)
CN (1) CN101333614B (ru)
CA (1) CA2689332A1 (ru)
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Cited By (5)

* Cited by examiner, † Cited by third party
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CN106399765A (zh) * 2016-10-11 2017-02-15 湖南理工学院 Al‑Si‑Mg铝合金及其制备工艺
US10113218B2 (en) 2014-03-31 2018-10-30 Hitachi Metals, Ltd. Cast Al—Si—Mg-based aluminum alloy having excellent specific rigidity, strength and ductility, and cast member and automobile road wheel made thereof
CN112941433A (zh) * 2019-12-11 2021-06-11 中国科学院金属研究所 一种改善6082铝合金停放效应的时效工艺
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* Cited by examiner, † Cited by third party
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CN102230114A (zh) * 2011-06-29 2011-11-02 北京科技大学 基于富Fe相优化的高硅铝合金及其制备方法
CN102747256A (zh) * 2012-06-19 2012-10-24 东南大学 一种铝硅基铝型材及其制备工艺
RU2525872C1 (ru) * 2013-04-23 2014-08-20 Федеральное Государственное Автономное Образовательное Учреждение Высшего Профессионального Образования "Сибирский Федеральный Университет" СПОСОБ ФОРМИРОВАНИЯ МИКРОСТРУКТУРЫ ЭВТЕКТИЧЕСКОГО Al-Si СПЛАВА
CN103769551B (zh) * 2014-01-17 2016-03-30 新疆众和股份有限公司 一种铝硅镁系铸造铝合金的生产工艺
CN104651763A (zh) * 2014-05-15 2015-05-27 巩向鹏 一种6063铝合金的性能优化方法
CN104087880B (zh) * 2014-07-08 2016-05-04 江苏佳铝实业股份有限公司 一种高阻尼铝硅合金板材的生产工艺
EP3228719B1 (en) * 2014-12-05 2021-03-03 Furukawa Electric Co., Ltd. Aluminum alloy wire rod, aluminum alloy stranded wire, covered wire, wire harness, and method for producing the aluminum alloy wire rod
JP6523681B2 (ja) * 2014-12-25 2019-06-05 株式会社Uacj ケース用アルミニウム合金板及びケース
CN105112744A (zh) * 2015-10-08 2015-12-02 江苏佳铝实业股份有限公司 一种高硅铝合金板材的制造工艺
TWI565808B (zh) * 2015-10-13 2017-01-11 財團法人工業技術研究院 鋁合金組成物及鋁合金物件的製造方法
FR3044326B1 (fr) * 2015-12-01 2017-12-01 Constellium Neuf-Brisach Tole mince a haute rigidite pour carrosserie automobile
CN105695811A (zh) * 2015-12-15 2016-06-22 东北大学 一种含Ti可时效强化高硅铝合金及其变形材制备方法
CN105695810B (zh) * 2015-12-15 2017-12-05 东北大学 一种含Mn可时效强化高硅铝合金及其变形材制备方法
CN106929781B (zh) * 2015-12-29 2019-01-08 徐工集团工程机械股份有限公司 一种高强度铝合金销轴的制备方法
CN106544606B (zh) * 2015-12-29 2018-05-01 徐工集团工程机械股份有限公司 一种耐磨铝合金销轴的制备方法
CN105671376B (zh) * 2016-01-26 2017-04-26 北京航空航天大学 高强高塑重力铸造与室温冷轧亚共晶铝硅合金材料及其制造方法
CA3166074A1 (en) 2017-12-21 2019-06-27 Novelis Inc. Aluminum alloy products exhibiting improved bond durability and/or having phosphorus-containing surfaces and methods of making the same
US11498839B2 (en) * 2019-06-01 2022-11-15 GM Global Technology Operations LLC Systems and methods for producing high-purity fine powders
CN113862534B (zh) * 2021-10-08 2022-07-29 上海交通大学 一种铝合金材料组织遗传性的调控方法及7085铝合金厚板的制备方法

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4077810A (en) * 1974-04-20 1978-03-07 Hitachi, Ltd. Aluminum alloys having improved mechanical properties and workability and method of making same
US5009844A (en) * 1989-12-01 1991-04-23 General Motors Corporation Process for manufacturing spheroidal hypoeutectic aluminum alloy
US20030143102A1 (en) * 2001-07-25 2003-07-31 Showa Denko K.K. Aluminum alloy excellent in cutting ability, aluminum alloy materials and manufacturing method thereof

Family Cites Families (26)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB582732A (en) * 1944-03-10 1946-11-26 Horace Campbell Hall Aluminium alloy having low coefficient of expansion
US4068645A (en) * 1973-04-16 1978-01-17 Comalco Aluminium (Bell Bay) Limited Aluminum-silicon alloys, cylinder blocks and bores, and method of making same
JPS5192709A (ja) * 1975-02-12 1976-08-14 Kakyoshoaruminiumuukeisokeigokinno shoshokeisobisaikaho
JPS52129607A (en) * 1976-04-23 1977-10-31 Hitachi Ltd Production of a1-si alloy having fine structure
JPS5669344A (en) * 1979-11-07 1981-06-10 Showa Alum Ind Kk Aluminum alloy for forging and its manufacture
JPS6283453A (ja) * 1985-10-07 1987-04-16 Sumitomo Alum Smelt Co Ltd 押出加工用アルミニウム合金鋳塊の製造法
JP2506115B2 (ja) * 1987-07-11 1996-06-12 株式会社豊田自動織機製作所 シャ−切断性の良い高強度・耐摩耗性アルミニウム合金とその製造法
JP3318966B2 (ja) * 1992-05-29 2002-08-26 日本軽金属株式会社 アルミニウム製スクロールの製造法
JPH06279904A (ja) * 1993-03-30 1994-10-04 Nippon Light Metal Co Ltd 鍛造用過共晶Ａｌ−Ｓｉ系合金及び鍛造用素材の製造方法
JPH0741920A (ja) * 1993-07-29 1995-02-10 Nippon Light Metal Co Ltd 耐摩耗性を向上させる過共晶Ａｌ−Ｓｉ合金の熱処理方法
JPH07197164A (ja) * 1993-12-28 1995-08-01 Furukawa Electric Co Ltd:The 高強度高加工性アルミニウム合金とその製造方法
JPH07224340A (ja) * 1994-02-14 1995-08-22 Nippon Light Metal Co Ltd 切削性に優れた過共晶Ａｌ−Ｓｉ合金及び製造方法
JPH083701A (ja) * 1994-06-15 1996-01-09 Mitsubishi Alum Co Ltd 強度と切削性にすぐれた耐摩耗性アルミニウム合金押出材の製造方法
JPH083674A (ja) * 1994-06-17 1996-01-09 Nissan Motor Co Ltd 過共晶Ａｌ−Ｓｉ合金および過共晶Ａｌ−Ｓｉ合金鋳物
JPH08176768A (ja) * 1994-12-22 1996-07-09 Nissan Motor Co Ltd 耐摩耗アルミニウム部材およびその製造方法
JP3835629B2 (ja) * 1996-09-24 2006-10-18 住友軽金属工業株式会社 切削性および耐食性に優れた耐摩耗性アルミニウム合金材
JP3261056B2 (ja) * 1997-01-14 2002-02-25 住友軽金属工業株式会社 陽極酸化皮膜の形成容易性および皮膜厚の均一性に優れた高強度耐摩耗性アルミニウム合金押出材およびその製造方法
KR100291560B1 (ko) * 1998-12-23 2001-06-01 박호군 내마모성이 우수하고 열팽창계수가 낮은 아공정 Al­Si단련용 합금 및 그의 제조방법과 그 합금의 이용
JP2001020047A (ja) * 1999-07-05 2001-01-23 Toyota Autom Loom Works Ltd アルミニウム合金鍛造用素材およびその製造方法
EP1413636B9 (en) * 2001-07-25 2009-10-21 Showa Denko K.K. Aluminum alloy excellent in machinability and aluminum alloy material and method for production thereof
JP2002206132A (ja) * 2001-11-27 2002-07-26 Kobe Steel Ltd 切削性に優れたアルミニウム合金押出材及びその製造方法
RU2221891C1 (ru) * 2002-04-23 2004-01-20 Региональный общественный фонд содействия защите интеллектуальной собственности Сплав на основе алюминия, изделие из этого сплава и способ изготовления изделия
CN1298878C (zh) * 2003-12-03 2007-02-07 东华大学 一种具有粒状硅相的铝硅合金系列及其制备方法
JP4474528B2 (ja) * 2004-11-01 2010-06-09 独立行政法人産業技術総合研究所 高靱性で鍛造成形可能な過共晶Ａｌ−Ｓｉ合金材料
CN100392129C (zh) * 2004-11-18 2008-06-04 东北大学 一种大尺寸过共晶高硅铝合金坯料及其制备方法
JP4773796B2 (ja) * 2005-10-28 2011-09-14 昭和電工株式会社 アルミニウム合金の連続鋳造棒、連続鋳造棒の鋳造方法、連続鋳造装置

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4077810A (en) * 1974-04-20 1978-03-07 Hitachi, Ltd. Aluminum alloys having improved mechanical properties and workability and method of making same
US5009844A (en) * 1989-12-01 1991-04-23 General Motors Corporation Process for manufacturing spheroidal hypoeutectic aluminum alloy
US20030143102A1 (en) * 2001-07-25 2003-07-31 Showa Denko K.K. Aluminum alloy excellent in cutting ability, aluminum alloy materials and manufacturing method thereof

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10113218B2 (en) 2014-03-31 2018-10-30 Hitachi Metals, Ltd. Cast Al—Si—Mg-based aluminum alloy having excellent specific rigidity, strength and ductility, and cast member and automobile road wheel made thereof
CN106399765A (zh) * 2016-10-11 2017-02-15 湖南理工学院 Al‑Si‑Mg铝合金及其制备工艺
CN112941433A (zh) * 2019-12-11 2021-06-11 中国科学院金属研究所 一种改善6082铝合金停放效应的时效工艺
CN113881907A (zh) * 2021-08-26 2022-01-04 山东创新金属科技有限公司 一种挤压铸造铝合金的时效处理工艺
CN115305391A (zh) * 2022-08-10 2022-11-08 中南大学 一种低能耗铝硅镁合金及其制备方法

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KR20100018048A (ko) 2010-02-16
RU2009149092A (ru) 2011-08-10
CA2689332A1 (en) 2009-01-08
CN101333614B (zh) 2010-09-01
EP2172572B1 (en) 2013-05-15
RU2463371C2 (ru) 2012-10-10
JP2010531388A (ja) 2010-09-24

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